Stable latexes of a chemically joined, phase separated thermoplastic graft copolymer and method for preparing the same

ABSTRACT

This application discloses a process for preparing a stable latex of a chemically joined, phase separated thermoplastic graft copolymer comprising: (1) copolymerizing: (a) from about 1 to about 95 percent by weight of a polymerizable macromolecular monomer comprising a linear polymer or copolymer having a molecular weight in the range of from about 5,000 to about 50,000 and having a substantially uniform molecular weight distribution, such that its ratio of Mw/Mn is less than about 1.1, said macromolecular monomer being further characterized as having no more than one polymerizable moiety per linear polymer of copolymer chain, said polymerizable moiety being on the end of the chain: and (b) from about 99 to about 5 percent by weight of at least one copolymerizable comonomer, said copolymerizable comonomers forming the polymeric backbones of said graft copolymer and said polymerizable macromolecular monomers forming the linear polymeric sidechains of said graft copolymer, and the linear polymeric sidechains of the graft copolymer are copolymerized into the backbone polymer through the polymerizable end group on said macromolecular monomer, and wherein said copolymerizable comonomer units of the backbone are comprised of polymerized ethylenically-unsaturated monomers, the linear polymeric sidechains of the graft copolymer which are copolymerized into the copolymeric backbone are separated by at least about 20 uninterrupted recurring monomeric units of said backbone polymer; the copolymerization and distribution of the sidechains along the backbone polymers being controlled by the relative reactivity ratios of the polymerizable end group on said macromolecular monomer and said copolymerizable comonomer; (2) said copolymerization being conducted in an aqueous latex copolymerization medium, wherein said polymerizable macromolecular monomer is dissolved in a small amount of a solvent therefor, and said solvent and polymerizable macromolecular monomer are emulsified in water by the action of an emulsifying agent during the copolymerization with said copolymerizable comonomer, said copolymerization being initiated by a polymerization catalyst which is soluble in the organic phase of the polymerization system; and (3) stopping the copolymerization prior to the formation of substantial amounts of homopolymers of said backbone polymer to thereby obtain a stable latex of a substantially pure, chemically joined, phase separated thermoplastic graft copolymer.

United States Patent [1 1 Schulz et al.

[ 1 Jan. 21, 1975 STABLE LATEXES OF A CHEMICALLY JOINED, PHASE SEPARATED THERMOPLASTIC GRAFT COPOLYMER AND METHOD FOR PREPARING THE SAME [75] Inventors: Gerald O. Schulz, Downers Grove;

Ralph Milkovich, Naperville, both of ill.

[73] Assigncc: CPC international lnc., Englewood Cliff, NJ.

[22] Filed: Aug. 3, 1973 21 Appl. No.: 385,500

Related US. Application Data [60] Division of Ser. No. 282,099, Aug. 21, 1972, Pat. No. 3,786,116, which is a continuation-in-part of Ser. No. 244,205, April 14, 1972, Pat. No. 3,832,423, which is a continuationin-part of Ser, No. 117,733, Feb. 22, 1971, abandoned.

[56] References Cited UNITED STATES PATENTS 3,235,626 2/1966 Waack 260/881 3,627,837 12/1971 Webb 260/836 3,691,126 9/1972 Walus 260/29.6 RW 3,716,506 2/1973 Simms et a1. 260/22 CB 3,786,116 1/1974 Milkovich et a1 260/885 OTHER PUBLICATIONS Black et al., Journal of Applied Polymer Science, Vol.

Primary Examiner-Melvin Goldstein Assistant ExaminerW. C. Danison Attorney, Agent, or Firm-Albert P. Halluin [57] ABSTRACT This application discloses a process for preparing a stable latex of a chemically joined, phase separated thermoplastic graft copolymer comprising: (1) copolymerizing: (a) from about 1 to about 95 percent by weight of a polymerizable macromolecular monomer comprising a linear polymer or copolymer having a molecular weight in the range of from about 5,000 to about 50,000 and having a substantially uniform mol cul a r weight distribution, such that its ratio of Mw/Mn is less than about 1.1, said macromolecular monomer being further characterized as having ,no more than one polymerizable moiety per linear polymer of copolymer chain, said polymerizable moiety being on the end of the chain: and (b) from about 99 to about 5 percent by weight of at least one copolymerizable comonomer, said copolymerizable comonomers forming the polymeric backbones of said graft copolymer and said polymerizable macromolecular monomers forming the linear polymericsidechains of said graft copolymer, and the linear polymeric sidechains of the graft copolymer are copolymerized into the backbone polymer through the polymerizable end group on said macromolecular monomer and wherein said copolymerizable comonomer units of the backbone are comprised of polymerized ethylenically unsaturated monomers, the linear polymeric sidechains of the graft copolymer which are copolymerized into the copolymeric backbone are separated by at least about 20 uninterrupted recurring monomeric units of said backbone polymer; the copolymerization and distribution of the sidechains along the backbone polymers being controlled by the relative reactivity ratios of the polymerizable end group on said macromolecular monomer and said copolymerizable comonomer; (2) said copolymerization being conducted in an aqueous latex copolymerization medium, wherein said polymerizable macromolecular monomer is dissolved in a small amount of a solvent therefor, and said solvent and polymerizable macromolecular monomer are emulsified in water by the action of an emulsifying agent during the copolymerization with said copolymerizable comonomer, said copolymerization being initiated by a polymerization catalyst which is soluble in the organic phase of the polymerization system; and (3) stopping the copolymerization prior to the formation of substantial amounts of homopolymers of said backbone polymer to thereby obtain a stable latex of a substantially pure, chemically joined, phase separated thermoplastic graft copolymer.

17 Claims, N0 Drawings STABLE LATEXES OF A CHEMICALLY JOINED, PHASE SEPARATED THERMOPLASTIC GRAFT COPOLYMER AND METHOD FOR PREPARING THE SAME CROSS-REFERENCE TO RELATED APPLICATIONS This application is a division of co-pending application Ser. No.'282,099, filed Aug. 21, 1972 now US. Pat. No. 3,786,116, granted Jan. 15, 1974. Application Ser. No. 282,099, is a continuation-in-part of copending application Ser. No. 244,205, filed Apr. 14, 1972 now U.S. Pat. No. 3,832,423, which in turn is a continuation-in-part of application Ser. No. 117,733, filed Feb. 22, 1971, said late application now abandoned.

BACKGROUND OF THE INVENTION 1. a. Statement of the Invention The present invention relates to chemically joined, phase separated thermoplastic graft copolymers and novel macromolecular monomers useful in the preparation of the graft copolymers.

2. b. Description of the Prior Art Polymer technology has developed to a high degree of sophistication and extensive research efforts in this direction are being undertaken to obtain improvements in polymer properties. Some of these efforts lead to polymer materials capable of competing with metals and ceramics in engineering applications. Generally, it is a requirement that these polymers be crystalline, since crystalline polymers are strong, tough, stiff and generally more resistant to solvents and chemicals than their non-crystalline counterparts.

Many poly alpha-olefins are crystalline and have excellent structural integrity; and, accordingly, have acquired increasing commercial acceptance as materials for competing with metals and ceramics. As one example, polyethylene has been regarded as one of the most important polymers among the major plastics, with its production reaching about 6 billion pounds in 1970 (1.7 billion pounds of high density linear polyethylene and 4.3 billion pounds of low density polyethylene).

Despite the widespread use of this important plastic, its use has been limited to flexible, translucent, molded articles or flexible, clear films, due'to its softness. The uses of polyethylene have also been limited due to its poor adhesion to many substrates and its low heat distortion, rendering it unsuitable for many high temperature applications.

Attempts by prior art workers to combine the properties of polyolefins and other polymers by either chemical or mechanical means generally has resulted in a sacrifice of many of the beneficial properties of both the polyolefin and the additional polymer. For example, graft copolymers of polyethylene and polypropylene have been prepared only with difficulty due to the inertness these polymers have with many other polymerizable monomers and polymers. The resultant graft copolymer generally has been a mixture which also contains free homopolymers.

Polyblends of a polyolefin with another polymer prepared by blending quantities of the two polymers together by mechanical means have been generally unsuitable for many applications due to their adverse solubility or extractability properties when used with various solvent systems, particularly when containing a rubbery, amorphous component.

The above considerations recognized by those skilled in the art with respect to the incompatibility of polyolefins with other polymers find almost equal applicability in the case of other plastics such as the polyacrylates, polymethacrylates, polyvinylchlorides, etc. Thus, the incompatibility of both natural and synthetic polymers becomes increasingly apparent as more and more polymers having particularly good properties for special uses have become available, and as efforts have been made to combine pairs of these polymers for the purpose of incorporating the different, good properties of each polymer into one product. More often than not, these efforts have been unsuccessful because the resulting blends have exhibited an instability, and in many cases the desirable properties of the new polymers were completely lost. As a specific example, polyethylene is incompatible with polystyrene and a blend of the two has poorer physical properties than either of the homopolymers. These failures were at first attributed to inadequate procedures, but eventually it was concluded that the failures were due simply to the inherent incompatibilities. Although it is now believed that this is a correct explanation, the general nature of such incompatibility has remained somewhat unclear, even to the present. Polarity seems to be a factor, i.e., two polar polymers are apt to be more compatible than a polar polymer and a non-polar polymer. Also, the two poly- .mers must be structurally and compositionally somewhat similar if they are to be compatible. Still further, a particular pair of polymers may be compatible only within a certain range of relative proportions of the two polymers; outside that range they are incompatible.

Despite the general acceptance of the fact of incompatibility of polymer pairs, there is much interest in devising means whereby the advantageous properties of combinations of polymers may be combined into one product.

One way in which this objective has been sought involves the preparation of block or graft copolymers. In this way, two different'polymeric segments, normally incompatible with one another, are joined together chemically to give a sort of forced compatibility. In such a copolymer, each polymer segment continues to manifest its independent polymer properties. Thus, the block or graft copolymer in many instances possesses a combination of properties not normally found in a homopolymer or a random copolymer I Recently, US. Pat. No. 3,235,626 to Waack, assigned to Dow Chemical Company, described a method for preparing graft copolymers of controlled branch configuration. It is described that the graft copolymers are prepared by first preparing a prepolymer by reacting a vinyl metal compound with an olefinic monomer to obtain a vinyl terminated prepolymer. After protonation and catalyst removal, the prepolymer is dissolved in an inert solvent with a polymerization catalyst and is thereafter reacted with either a different polymer having a reactive vinyl group or a different vinyl monomer under free-radical conditions.

The current limitations on the preparation of these copolymers are mechanistic. Thus, there is no means for controlling the spacing of the sidechains along the backbone chain and the possibility of the sidechains having irregular sizes. Due to the mechanistic limitations of the prior art methods, i.e., the use of an alphaolefin terminated prepolymer with acrylonitrile or an acrylate monomer, complicated mixtures of free homopolymers result.

In view of the above considerations, it would be highly desirable to devise a means for preparing graft copolymers wherein the production of complicated mixtures of free homopolymers is minimized and the beneficial properties of the sidechain and backbone polymer are combined in one product.

Moreover, it is recognized and documented in the literature, such as R. Waack et al., Polymer, Vol. 2, pp. 365-366 (1961), and R. Waack et al., J. Org. Chem., Vol. 32, pp, 3,395-3,399 (1967), that vinyl lithium is one of the slowest anionic polymerization initiators. The slow initiator characteristic of vinyl lithium when used to polymerize styrene produces a polymer having a broad molecular weight distribution due to the ratio of the overall rate of propagation of the styryl anion to that of the vinyl lithium initiation. In other words, the molecular weight distribution of the polymer produced will be determined by the effective reactivity of the initiator compared with that of the propagating anionic polymer species, i.e., vinyl lithium initiator reactivity compared to the styryl anion. Accordingly, following the practice of US. Pat. No. 3,235,626, a graft copolymer having sidechains of uniform molecular weight cannot be prepared.

US. Pat. Nos. 3,390,206 and 3,514,500 describe processes for terminating free-radical and ionic polymerized polymers with functional groups which are described as capable of copolymerizing with polymerizable monomers. The functionally terminated prepolymers described by these patentees also would be expected to have a broad molecular weight distribution and, therefore, would not be capable of producing a chemically joined, phase separated thermoplastic graft copolymer.

SUMMARY OF THE INVENTION The present invention relates to thermoplastic graft copolymers comprised of copolymeric backbones containing a plurality of uninterrupted repeating units of the backbone polymer and at least one integrally copolymerized moiety per backbone polymer chain having chemically bonded thereto a substantially linear polymer which forms a copolymerized sidechain to the backbone, wherein each of the polymeric sidechains has substantially the same molecular weight and each polymeric sidechain is chemically bonded to only one backbone polymer.

The graft copolymers of the present invention assume a T-type structure when only one sidechain is copolymerized into the copolymeric backbone. However, when more than one sidechain is copolymerized into the backbone polymer, the graft copolymer may be characterized as having a comb-type structure illustrated in the following manner:

c-c-c-b-c-c-c-b-c-cc-b-c-cc l a a L l l I a a a l I a a a wherein a represents a substantially linear, uniform molecular weight polymer or copolymer having a suffirupted recurring monomeric units in each segment. It

has been found that this condition provides the graft copolymer the properties of the polymer. In other words, the presence of segments containing at least about 20 uninterrupted recurring monomeric units provides the graft copolymers with the physical properties attributed to this polymer, such as crystalline melting point (Tm) and structural integrity.

The backbone polymeric segments of the chemically joined, phase separated thermoplastic graft copolymers of the present invention are derived from copolymerizable monomers, preferably the low molecular weight monomers. These copolymerizable monomers include polycarboxylic acids, their anhydrides and amides, polyisocyanates, organic epoxides, including the thioepoxides, urea-formaldehydes, siloxanes, and ethylenically unsaturated monomers. A particularly preferred group of copolymerizable monomers include the ethylenically-unsaturated monomers, especially the monomeric vinylidene type compounds, i.e., monomers containing at least one vinylidene wherein a hydrogen is attached to one of the free valences of the vinylidene group are contemplated as falling within the generic scope of the vinylidene compounds referred to hereinabove.

The copolymerizable monomers useful in the practice of the present invention are not limited by the exemplary classes of compounds mentioned above. The only limitation on the particular monomers to be employed is their capability to copolymerize with the polymerizable end groups of the sidechain prepolymer under free-radical, ionic, condensation, or coordination (Ziegler or Ziegler-Natta catalysis) polymerization reactions. As it will be seen from the description of macromolecular monomers, described hereinbelow, the choice of polymerizable end groups includes any polymerizable compound commercially available. Accordingly, the choice of respective polymerizable end group and copolymerizable monomer can be chosen, based upon relative reactivity ratios under the respective copolymerization reaction conditions suitable for copolymerization reaction. For example, alpha-olefins copolymerize with one another using Ziegler catalysts, and acrylates copolymerize with vinyl chloride, acrylonitrile and other alkyl acrylates. Accordingly, an alphaoleiin terminated macromolecular monomer copolymerizes with ethylene and-alpha-olefins using a Ziegler catalyst and an acrylate or methacrylate terminated macromolecular monomer copolymerizes with vinyl chloride, acrylonitrile, acrylates and methacrylates rated monomers as the backbone comonomer generunder free-radical conditions in a manner governed by ally correspond to the following structural formula:

I Rn

the respective reactivity ratios for the comonomers. wherein R and R" are each selected from the group As will be explained hereinafter, the excellent combiconsisting of hydrogen, lower alkyl, cycloalkyl, and aryl nation of beneficial properties possessed by the graft radicals; X and X are each selected from the group copolymers of the present invention are attributed to onsisting of hydrogen, alkylene radica -l' the large segments of uninterrupted copolymeric back- 2}; bones and the integrally copolymerized lin ar sid x is a positive integer wherein the terminal methylene l5 chains of controlled molecular weight and narrow mogroup in X 18 either hydrogen, lower alkyl, e.g., methyl, lecular weight distribution. halogen, etc., and in the case of X, joins the backbone The term linear, referred to hereinabove, is being polymer with the sidechain polymer), a saturated ester used in its conventional sense, to pertain to a polymeric backbone that is free from cross-linking.

. 20 O The sidechain polymers having substantially uniform I molecular weight are comprised of substantially linear C OR or 0 C R polymers and copolymers produced by anionic polymerization of any anionically polymerizable monomer, wherein R is a1ky] or aryl), i il (L E as will be described hereinafter. Preferably, the sideamide (i'e. chain polymer will be different than the backbone polymer. R

It is preferred that at least one segment of the side- -c N chain polymer of the graft copolymers of the present n. invention have a molecular weight sufficient to manifest the beneficial properties of the respective polymer. wh i R and R" are eitherhydrogen, alkyl or aryl In other words, physical properties of the sidechain di l amine (i,e., polymer such as the glass transition temperature (Tg) will be manifest. Generally, as known in the art, the average molecular weight of the segment of the polymeric sidechains necessary to establish the physical properties of the polymer will be from about 5,000 to about 50,000. wherein R and R" are either hydrogen, alkyl or aryl In light of the unusual and improved physical properradicals), isocyanate, halogen (i.e., F, Cl, Br or I) and ties possessed by the thermoplastic graft copolymers of 40 eth (i,e O-R, wherein R is either alkyl or aryl the present invention, itis believed that the monofuncradicals); X and X may be the same or different, H tionally bonded polymeric sidechains having substanr, i th as wh re X is an ester, X should be a tlally uniform molecular Weight form What is known as functional group such as ester, halogen, nitrile, etc., as domains. explained hereinabove with respect to the respective STATEMENT OF THE INVENTXON reactivity ratios of the comonomers used to prepare the graft copolymers, Y IS a substantially linear polymer or Briefly, the chemically joined, Phase separa ed the copolymer wherein at least one segment of the polymer moplastic graft copolymers of the present invention are has a sufficient molecular weight to manifest the propprepared by first preparing the sidechains in the form erties of the resepctive polymer, i.e., a molecular of monofunctional living polymers of substantially uniweight of from about 5,000 to about 50,000, preferably form molecular weight. The living polymers are therea m lecular weight of from about 10,000 to about after terminated, as by reaction with a halogen- 35,000, more preferably 12,000 to about 25,000; the containing compound that also contains a reactive symbols a, b and c are positive integers, with the propolymerizable group, such as, for example, a polymerviso that a and b are each a value such that the physical izable fini 0 p xy g up, r a p und which properties of the uninterrupted segments in the backcontains a reactive site to an anion of the living polybone, e g,, Tm, are manifest, preferably at least about mer and a polymerizable moiety which does not prefer- 20; and the symbol 0 is at least one, but preferably ential y e ct With the anion, 8-, mflleic yd ide greater than one, e.g., a value such that the molecular The monofunctional terminated living polymer chains weight of the graft copolymer will be up to about are then polymerized, together with the backbone 2,000,000.

monomer, to form a chemically joined. phase separated The formation of the graft copolymers of the present thermoplastic graft copolymer wherein the polymeric invention may be better understood by reference to the sidechains are integrally polymerized into the backfollowing reactions illustrated by the equations set bone polymer. forth below whereinhthe invegtiorli is iklltistratted ilpbterms of 01 st rene sidec ains an po yet y ene ac ones.

DESCRIPTION OF THE PREFERRED lt fan be seen from these equations that the first reac- EMBODIMENTS tions involve the preparation of living polymers of poly- The chemically joined, phase separated thermoplasstyrene. The living polymers are thereafter reacted with tic graft copolymers derived from ethylenically unsatua molar equivalent of allyl chloride, wherein the reaction takes place at the carbon-chloride bond, rather than at the carbon-carbon double bond. The vinyl terminated polystyrene, referred to herein as the alphaolefin terminated macromolecular monomer, is then copolymerized with ethylene to produce a graft copolymer of polyethylene, whereby the vinyl moiety of the polystyrene is integrally polymerized into the linear polyethylene backbone.

Alternatively, the living polymer can be reacted with an epoxide such as, for example, ethylene oxide, to produce a alkoxide ion which can then be reacted with the halogen-containing olefin, i.e., allyl chloride, to produce an alpha'olefin terminated macromolecular monomer. This, in essence, places the terminal alphaolefin farther away from the aromatic ring of the polystyrene and therefore reduces any steric hindering influence that might be exerted by the aromatic ring.

FORMATION OF THE GRAFT COPOLYMER OF ALPHA-OLEFIN TERM INATED POLYSTYRENE SIDECHAIN AND POLYETHYLENE BACKBONE Initiation: CH CH (CH )CHLi CH2 fin v e 69 ca ca (ca )cucu cu Li Propag ation: (n--l)Cl-l CH In the equations above, the symbols a, b, c, n and X are positive integers whererin a and b are at least about 20, n has a value of from about 50 to about 500, and x has a value corresponding approximately to the sum of a and b.

PREPARATION OF THE LIVING POLYMERS The sidechains of the chemically joined, phase separated graft copolymers, above, are preferably prepared by the anionic polymerization of a polymcrizablc 'monomer or combination of monomers. In most in- 0 inert organic diluent which does not participate in or interfere with the polymerization reaction.

-= CH Polymerization Catalyst e I 9 CH CH (CH )C CH CH (lH CH Li Termination with Active End Group: CH CHCH CI CH CH (CH )C H CH I CH CH CH LiCl Craft Copolgerization: xCH

a CH

CH CH (CH ):CH CH -CH Those monomers susceptible to anionic polymerization are well-known and the present invention contemplates the use of all anionically polymerizable monomers. Non-limiting illustrative species include vinyl aromatic compounds, such as styrene, alphamethylstyrene, vinyl toluene and its isomers; vinyl unsaturated amides such as acrylamide, methacrylamide, N,N-dilower alkyl acrylamides, e.g., N,N- dimethylacrylamide; acenaphthalene; 9- acrylcarbazole; acrylonitrile and methacrylonitrile; organic isocyanates including lower alkyl, phenyl, lower alkyl phenyl and halophenyl isocyanates, organic diisocyanates including lower alkylene, phenylene and tolylene diisocyanates; lower alkyl and allyl acrylates and methacrylates including methyl, t-butyl acrylates and methacrylates; lower olefins, such as ethylene, propylene, butylene, isobutylene, pentene, hexene, etc.; vinyl esters of aliphatic carboxylic acids such as vinyl acetate, vinyl propionate, vinyl octoate, vinyl oleate, vinyl stearate, vinyl benzoate; vinyl lower alkyl ethers; vinyl pyridines, vinyl pyrrolidones; dienes including isoprene and butadiene. The term lower is used above to denote organic groups containing 8 or fewer carbon atoms. The preferred olefinic containing monomers are conjugated dienes containing 4 to 12 carbon atoms per molecule and the vinyl-substituted aromatic hydrocarbons containing up to about 12 carbon atoms.

Many other monomers suitable for the preparation of the sidechains by anionic polymerization are those disclosed in Macromolecular Reviews: Volume 2, pages 74-83, Interscience Publishers, Inc. (1967), entitled Monomers Polymerized by Anionic initiators, the disclosure of which is incorporated herein by reference:

The initiators for these anionic polymerizations are any alkali metal hydrocarbons and alkoxide salts which produce a monofunctional living polymer, i.e., only one end of the polymer contains a reactive anion. Those catalysts found suitable include the hydrocarbons of lithium, sodium or potassium as represented by the formula RMe wherein Me is an alkali metal such as sodium, lithium or potassium and R represents a hydrocarbon radical, for example, an alkyl radical containing up to about carbon atoms or more, and preferably up to about 8 carbon atoms, an aryl radical, an alkaryl radical or an aralkyl radical. Illustrative alkali metal hydrocarbons include ethyl sodium, n-propyl sodium, nbutyl potassium, n-octyl potassium, phenyl sodium, ethyl lithium, sec-butyl lithium, t-butyl lithium and 2- ethylhexyl lithium. Sec-butyl lithium is the preferred initiator because it has a fast initiation which is important in preparing polymers of narrow molecular weight distribution. It is preferred to employ the alkali metal salts of tertiary alcohols, such as potassium t-butyl alkoxylate, when polymerizing monomers having a nitrile or carbonyl functional group.

The alkali metal hydrocarbons and alkoxylates are either available commercially or may be prepared by known methods, such as by the reaction of a halohydrocarbon, halobenzene or alcohol and the appropriate alkali metal.

An inert solvent generally is used to facilitate heat transfer and adequate mixing ofinitiator and monomer. Hydrocarbons and ethers are the preferred solvents. Solvents useful in the anionic polymerization process include the aromatic hydrocarbons such as benzene, toluene, xylene, ethylbenzene, t-butylbenzene, etc.

Also suitable are the saturated aliphatic and cycloaliphatic hydrocarbons such as n-hexane, n-heptane, noctane, cyclohexane and the like. In addition, aliphatic and cyclic ether solvents can be used, for example, dimethyl ether, diethyl ether, dibutyl ether, tetrahydrofuran, dioxane, anisole, tetrahydropyran, diglyme, glyme, etc. The rates of polymerization are faster in the ether solvents than in the hydrocarbon solvents, and small amounts of ether in the hydrocarbon solvent in crease the rates of polymerization.

The amount of initiator is an important factor in anionic polymerization because it determines the molecular weight of the living polymer. If a small proportion ofinitiator is used, with respect to the amount of monomer, the molecular weight of the living polymer will be larger than if a large proportion of initiator is used. Generally, it is advisable to add initiator dropwise to the monomer (when that is the selected order of addition) until the persistence of the characteristic color of the organic anion, then add the calculated amount of initiator for the molecular weight desired. The preliminary dropwise addition serves to destroy contaminants and thus permits better control of the polymerization.

To prepare a polymer of narrow molecular weight distribution, it is generally preferred to introduce all of the reactive species into the system at the same time. By this technique, polymer growth by consecutive addition of monomer takes place at the same rate to an active terminal group, without chain transfer or termination reaction. When this is accomplished, the molecular weight of the polymer is controlled by the ratio of monomer to initiator, as seen from the following representation:

Molecular weight of living polymer g i ldoleeular Weight of Monomer As it can be seen from the above formula, high concentrations of initiator leads to the formation of low molecular weight polymers, whereas, low concentrations of initiator leads to the production of high molecular weight polymers.

The concentration of the monomer charged to the reaction vessel can vary widely, and is limited by the ability of the reaction equipment to dissipate the heat of polymerization and to properly mix the resulting viscous solutions of the living polymer. Concentrations of monomer as high as 50 percent by weight or higher based on the weight of the reaction mixture can be used. However, the preferred monomer concentration is from about 5 to about 25 percent in order to achieve adequate mixing.

As can be seen from the formula above and the foregoing limitations on the concentration ofthe monomer,

'the initiator concentration is critical, but may be varied according to the desired molecular weight of the living polymer and the relative concentration of the monomer. Generally, the initiator concentration can range from about 0.001 to about 0.1 mole of active alkali metal per mole of monomer, or higher. Preferably, the concentration of the initiator will be from about 0.0] to about 0.004 mole of active alkali metal per mole of monomer.

The temperature of the polymerization will depend on the monomer. Generally, the reaction can be carried out at temperatures ranging from about l00C up to about C. When using aliphatic and hydrocarbon diluents, the preferred temperature range is from about lC to about 100C. With ethers as the solvent, the preferred temperature range is from about l00C to about 100C. The polymerization of the styrene is generally carried out at slightly above room temperature; the polymerization of alpha-methylstyrene preferably is carried out at lower temperatures, e.g., 80C.

The preparation of the living polymer can be carried out by adding a solution of the alkali metal hydrocarbon initiator in an inert organic solvent to a mixture of monomer and diluent at the desired polymerization temperature and allowing the mixture to stand with or without agitation until the polymerization is completed. An alternative procedure is to add monomer to a solution of the catalyst in the diluent at the desired polymerization temperature at the same rate that it is being polymerized. By either method the monomer is converted quantitatively to a living polymer as long as the system remains free of impurities which inactivate the anionic species. As pointed out above, however, it is important to add all of the reactive ingredients together rapidly to insure the formation of a uniform molecular weight distribution of the polymer.

The anionic polymerization must be carried out under carefully controlled conditions, so as to exclude substances which destroy the catalytic effect of the catalyst or initiator. For example, such impurities as water, oxygen, carbon monoxide, carbon dioxide, and the like. Thus, the polymerizations are generally carried out in dry equipment, using anhydrous reactants, and

under an inert gas atmosphere, such as nitrogen, helium, argon, methane, andthe like.

The above-described living polymers are susceptible to furtherreactions including further polymerization. Thus, if additional monomer, such as styrene, is added to the living polymer, the polymerization is renewed and the chain grows until no more monomeric styrene remains. Alternatively, if another different anionically polymerizable monomer is added, such as butadiene or ethylene oxide, the above-described living polymer initiates the polymerization of the butadiene or ethylene oxide and the ultimate living polymer which results consists of a polystyrene segment and a polybutadiene or polyoxyethylene segment.

A poly(styrene-ethylene) block copolymer can be prepared by contacting living polystyrene with ethylene in the presence of a compound of a transition metal of Group V-VIII in the periodic table, e.g., titanium tetrachloride. This technique is also applicable to the alpha- Living Pol e r:

Terminating Agents:

olefins, such as propylene. The resulting copolymer is still a living polymer and can be terminated by the methods in accordance to the practice of the present invention. I

As noted above, the living polymers employed in the present invention are characterized by relatively uni form molecular weight, i.e., the distribution of molecular weights of the mixture of living polymers produced is quite narrow. This is in marked contrast to the typical polymer, where the molecular weight distribution is quite broad. The difference in molecular weight distribution is particularly evident from an analysis of the gel permeation chromatogram of commercial polystyrene (Dow 666u) prepared by free-radical polymerization and polystyrene produced by the anionic polymerization process utilized in accordance with the practice of the present invention.

PRODUCTION OF THE MACROMOLECULAR MONOMERS BY TERMINATION OF THE LIVING POLYMERS The living polymers herein are terminated by reaction with a halogen-containing compound which also contains a polymerizable moiety, such as an olefinic group or an epoxy or thioepoxy group. Suitable halogen-containing terminating agents include: the vinyl haloalkyl ethers wherein the alkyl groups contain six or fewer carbon atoms such as methyl, ethyl, propyl, butyl, isobuty], sec-butyl, amyl or hexyl; vinyl'esters of haloalkanoic acids wherein the alkanoic acid contains six or fewer carbon atoms, such as acetic, propanoic, butyric, pentanoic, or hexanoic acid; olefinic halides having six or fewer carbon atoms such as vinyl halide, allyl halide, methallyl halide, 6-halo-1-hexene, etc.; halides of dienes such as 2-halomethyl-l,3-butadiene, epihalohydrins, acrylyl and methacrylyl halides, haloalkylmaleic anhydrides; haloalkylmaleate esters; vinyl haloalkylsilanes; vinyl haloaryls; and vinyl haloalkaryls,

such as vinylbenzyl chloride (VBC); haloalkyl norbor-.

nenes, such as bromomethyl norbornene, 'bromonorbornane, and epoxy compounds such as .ethylene or propylene oxide. The halo group may be chloro, fluoro,

CH Li -'and R C---C(JOR In the above equations, R, R, R R and R are each selected from the group consisting of hydrogen and lower alkyl, and aryl radicals. Preferably, will be lower alkyl, 'such as secbutyl; R will be either hydrogen or methyl; R will be phenyl; R will be hydrogen or lwoer alkylene radicalyand R will be either hydrogen or lower alkyl radical. The symbol n is a positive integer such that the properties of the polymer are manifest, i.e., a value such that the polymer will have a molecularweight in the range of from about 5,000 to about 50,000, preferably a molecular weight in the range of from about 10,000 to about 35,000, more preferably a molecular weight in the range of from about 12,000 to about 25,000.

Termination of the living polymer by any of the above types of terminating agents is accomplished simply by adding the terminating agent to the solution of living polymer at the temperature at which the living polymer is prepared. Reaction is immediate and the yield is theoretical. A slight molar excess of the terminating agent, with respect to the amount of catalyst, may be used although the reaction proceeds on a molefor-mole basis.

The termination may be conducted in any suitable inert solvent. Generally, it is advisable to utilize the same solvent system employed in the preparation of the living polymer. A preferred embodiment of the invention comprises conducting the termination reaction in a hydrocarbon solvent rather than the polar ether type solvents such as tetrahydrofuran. It has been found that the hydrocarbon solvents such as the aromatic hydrocarbons, saturated aliphatic and cycloaliphatic hydrocarbons cause several differences'in the reaction conditions and the resulting product. For example, the termination reaction can be conducted at higher temperatures with hydrocarbon solventsas opposed to the ether solvents.

In some instances, because of the nature of the living polymer and the monomer from which it is prepared, or because of the nature of the terminating agent, certain deleterious side reactions occur which result in an impure product. For example, the carbanion of some living polymers have a tendency to react with functional groups or any active hydrogens of the terminatv one of the active hydrocarbons of the acrylyl or methacrylyl chloride.

It has been discovered that one means for overcoming the foregoing problem is to render the reactive carbanion less susceptible to reaction with the functional groups or any active hydrogens of a terminating agent. A preferred method to render the living polymer less susceptible to the adverse reaction is to cap the highly reactive living polymer with a lesser reactive reactant. Examples of some preferred capping agents" include the lower alkylene oxides, i.e., one having eight or fewer carbon atoms such as ethylene and propylene oxide; diphenyl ethylene, etc. The capping reaction yields a product which still is a living polymer, but yields a purer product when subsequently reacted with cu 6-6-01 is ca -cu -(cn ca 0) cu ca 0 m I will 2 2 2 x 2 2- ll sec-Bu Ca -cu (cu c11 0) cn cn octlz 011 LiCl a terminating agent containing a functional group or active hydrogen,

[t has been found that diphenyl ethylene is an excellent capping agent when'terminating agents such as, for example, vinyl chloroalkanoates are employed.

A particularly preferred capping agent is an alkylene oxide, such as ethylene oxide. It reacts with the liv- 9 (*3 sec-Bu a ca cu CH Li cu cuv sec-Bu on on CH QH-CH CH O Li tri wherein n is a positive integer of about at least 50, x is either 0 or a positive integer and R is either hydrogen or methyl.

When an epihalohydrin is used as the terminating reagent, the resulting polymer contains a terminal epoxy group. This terminal epoxy may be used as the poly merizable group itself, such as in the preparation of a polyisobutylene or a polypropylene oxide backbone graft copolymer or may be converted to various other useful polymerizable end groups by any one of several known reactions.

As one embodiment of the invention, the terminated polymer containing an epoxy or thioepoxy end group The capping reaction is carried out quite simply, as may be reacted with a polymerizable carboxylic acid in the case of the terminating reaction, by adding the capping reactant to the living polymer at polymeriza tion temperatures. The reaction occurs immediately. As in the case of the termination reaction, a slight molar excess of the capping reactant with respect to the amount of initiator may be used. The reaction occurs on a mole-for-rnole basis.

It will be understood that when a large molar excess of alkylene oxide is reacted with the living polymer, a living polymer having two polymeric blocks is produced. A typical example with polystyrene segments and polyoxyalkylene segments is illustrated as follows:

halide, such as acrylic, methacrylic, or maleic acid halide, to produce a beta-hydroxyalkyl acrylate, methacrylate or maleate ester as the polymerizable terminal moiety of the substantially uniform molecular weight polymer. These same polymerizable esters may be prepared from the terminal epoxy polymer by first converting the epoxy group to the corresponding glycol by warming the polymer with aqueous sodium hydroxide, followed by conventional esterification of the glycol end group with the appropriate polymerizable carboxylic acid, or acid halide.

The resulting glycol obtained by the aqueous hydrolysis of the epoxy group in the presence of a base may be converted to a copolymer by reaction with a high molecular weight dicarboxylic acid which may be prepared, e.g., by the polymerization of a glycol or diamine with a molar excess of phthalic anhydride, maleic anhydride, succinic anhydride, or the like. These reactions can be modified to obtain a polystyrene block and a polyamide block (Nylon). The glycol terminated polymer may also be reacted with a diisocyanate to form a polyurethane. The diisocyanate may be e.g., the reaction product ofa polyethylene glycol having an average molecular weight of 400 with a molar excess of phenylene diisocyanate.

in another embodiment of the invention, an organic epoxide is copolymerized with a terminated polymer containing an epoxy or thioepoxy end group. The graft copolymer which results is characterized by a backbone having uninterrupted segments of at least about 20, and preferably at least about 30, recurring units of the organic epoxide. Preferred organic epoxides include ethylene oxide, propylene oxide, butylene oxide, hexylene oxide, cyclohexene epoxide and styrene oxide, i.e., those having 8 or fewer carbon atoms.

When a haloalkylmaleic anhydride or haloalkylmaleate ester is used as the terminating agent, the resulting terminal groups can be converted by hydrolysis to carboxyl groups. The resulting dicarboxylic polymer may be copolymerized with glycols or diamines to form polyesters and polyamides having a graft copolymer structure.

If it is desired to isolate and further purify the macromolecular monomer from the solvent from which it was prepared, any of the known techniques used by those skilled in the art in recovering polymeric materials may be used. These techniques include: (1) solvent-nonsolvent precipitation; (2) evaporation of solvent in an aqueous media; and (3) evaporation of solvent, such as by vacuum roll drying, spray drying, freeze drying; and (4) steam jet coagulation.

The isolation and recovery of the macromolecular monomer is not a critical feature of the invention. In fact, the macromolecular monomer need not be recovered at all. Stated otherwise, the macromolecular,

monomer, once formed, can be charged with the suitable monomer and polymerization catalyst to conduct the graft copolymerization in the same system as the macromolecular monomer was prepared, providing the solvent and materials in the macromolecular monomer preparation reactor do not poison the catalyst or act in a deleterious manner to the graft copolymerization process. Thus, a judicious selection of the solvent and purification of the reactor system in the preparation of the macromolecular monomer can ultimately result in a large savings in the production of the graft copolymers of the present invention.

As pointed out above, the macromolecular monomers, which ultimately become the sidechains of the graft copolymers by being integrally polymerized into the backbone polymer, must have a narrow molecular weight distribution. Methods for determining the molecular weight distribution of polymers'such as the macromolecular monomers are known in the art. Using these known methods, the weight average molecular weight (Mw) and the number average molecular weight (Mn) can be ascertained, and the molecular weight distribution (MW/Mn) for the macromolecular.

monomer can be determined. The macromolecular monomers must have nearly a Poisson molecular weight distribution or be virtually monodisperse in order to have the highest degree of functionality. Preferably, the ratio of Mw/K'fn of the novel macromolecular monomers will be less than about 1.1. The macromolecular monomers of the present invention possess the aforementioned narrow molecular weight distribution and purity due to the method of their preparation, described hereinabove. Thus, it is important that the sequence of steps in preparing the macromolecular monomers be adhered to in order toproduce the optimum results in beneficial properties in the graft copolymers.

GRAFT COPOLYMERIZATION Prior to the invention herein, graft copolymers were prepared by synthesizing a linear backbone, then grafting onto his backbone, growing polymeric or preformed polymeric chains. These methods generally re quire elaborate equipment and produce a mixture of products having inferior properties unless further purified. Because of the additional processing conditions and the use of special equipment, these processes are not economically feasible.

Although some of the prior art graft copolymers, such as those described in U.S. Pat. Nos. 3,627,837, 3,634,548 and 3,644,584 and British Pat. Nos. 873,656 and l,l44,l5l resemble the graft copolymers of the present invention. Generally, the present graft copolymers are different compositions, not only because they are prepared by significantly different processes, but because the pendant polymeric chains of the graft copolymers of this invention are of relatively uniform, minimum length, and are each an integral part of the backbone. Furthermore, the backbone of the graft copolymers of the present invention contain polymeric segments of certain minimum length. Thus, the present graft copolymers differ structurally because the macromolecular monomer is interposed between polymeric segments of the backbone polymer, rather than being merely attached to the backbone polymer in a random manner. These characteristics contribute materially to the advantageous properties which inhere in these novel graft copolymers.

The graft copolymers of the present invention are prepared by first synthesizing the pendant polymeric chains (the polymerizable terminated living polymers) then copolymerizing the terminal portions of the polymeric chains with the second monomer during the formation of the backbone polymer.

In accordance with the practice of the present invention, the substantially pure macromolecular monomers of high controlled molecular weight and molecular weight distribution have an appropriate reactive end group suitable for any mechanism of copolymerization, e.g., free-radical, cationic, anionic, Ziegler catalysis, and condensation. Thus, the reactive end group is selected for easy copolymerization with low cost monomers by conventional means and within existing polymerization equipment.

The copolymerization with the macromolecular monomers and the second reactive monomer is a graftlike structure where the pendant chain is a polymer whose molecular weight and distribution are predetermined by independent synthesis. The distribution of the sidechain polymer along the backbone is controlled by the reactivity ratios of the comonomers.

Since the reactive end group of the macromolecular monomer is copolymerized with the second monomer, it is an integral part of the backbone polymer. Thus, the polymerizable end group of the macromolecular monomer is interposed between large segments of the backbone polymer.

The present invention provides a means for controlling the structure of the graft copolymer. More specifically, the control of the structure of the graft copoly mer can be accomplished by any one or all of the following means: (1 by determining the reactivity ratio of the macromolecular monomer and a second monomer during the copolymerization reaction, a pure graft polymer free from contamination by homopolymers can be prepared; (2) by controlling the monomer addition rates during the copolymerization of a macromolecular monomer and a second monomer, the distance between the sidechains in the polymer structure can be controlled; and (3) the size of the graft chain can be predetermined and controlled in the anionic polymerization step of the preparation of the macromolecular monomer.

It will be apparent to those skilled in the art that by the proper selection of, terminating agents, all mechanisms of copolymerization may be employed in preparing the controlled phase separated graft copolymers.

As alluded to hereinabove, the chemically joined, phase separated graft copolymers of the present inven tion are preferably copolymerized with any ethylenically-unsaturated monomer including the vinylidene type compounds containing at least one vinylidene group and preferably the vinyl-type compounds containing the characteristic CH CH- group wherein hydrogen is attached to one of the free valences of the vinylidene group. The copolymerization, as pointed out above, is only dependent upon the relative reactivity ratios of the terminal group and the comonomer.

Examples of some of the preferred ethylenicallyunsaturated compounds used as the comonomers include the acrylic acids, their esters, amides and nitriles including acrylic acid, methacrylic acid, the alkyl esters of acrylic and methacrylic acid, acrylonitrile, methacrylonitrile, acrylamide, methacrylamide, N,N- dimethacrylamide (NNDMA); the vinyl halides such as vinyl chloride, and vinylidene chloride; the vinyl cyanides such as vinylidene cyanide (1,1- dicyanoethylene); the vinyl esters of the fatty acids such as vinyl acetate, vinyl propionate and vinyl chloroacetate, etc.; and the vinylidene containing dicarboxylic anhydrides, acids and esters, fumaric acid and esters, maleic anhydrides, acids and esters thereof.

A particularly important class of vinylidene type compounds useful as comonomers with the alphaolefin and styrene terminated macromolecular monomers include the vinyl olefinic hydrocarbons, such as ethylene, propylene, l-butene, isobutylene, l-pentene, l-hexene, styrene, 3-methyl-l-butene, 4-methyl-lhexene and cyclohexene. Also, there may be used as the comonomers the polyolefinic materials containing at least one vinylidene group such as the butadienel,3hydrocarbons including butadiene, isoprene, piperylene and other conjugated dienes, as well as other conjugated and non-conjugated polyolefinic monomers in cluding divinyl benzene, the diacrylate type esters of methylene, ethylene, polyethylene glycols, and polyallyl sucrose.

The most preferred ethylenically unsaturated comonomers are the commercially available and wisely used monomers such as methyl acrylate, butyl acrylate, 2- ethyl hexyl acrylate, methyl methacrylate, vinyl chloride, vinylidene chloride, vinylidene cyanide, acrylonitrile; and the hydrocarbon monomers such as ethylene, propylene, styrene; and the conjugated dienes such as butadiene and isoprene.

In addition to the hereinabove described ethylenically-unsaturated comonomers useful in the practice of the invention, there are included the comonomers capable of copolymerizing by condensation or stepreaction polymerization conditions with the polymerizable macromolecular monomers of the invention. in this connection, the polymerizable macromolecular monomers will contain the appropriate terminal groups necessary to facilitate the condensation reaction. For example, living polymers terminated with epichlorohydrin will contain an epoxy terminal group which converts to a l -CH CH group upon saponification. This vicinal hydroxy group is capable of copolymerizing with polybasic acids and anhydrides to form polyesters, such as adipic acid, phthalic anhydride, maleic anhydride, su'ccinic anhydride, trimellitic anhydride, etc.; aldehydes to form polyacetals, such as polyformaldehyde, ureaformaldehydes, acetaldehydes, etc.; polyisocyanates and polyisocyanate prepolymers to form polyurethanes; and siloxanes to form polysiloxanes. The living polymers terminated. with halomaleic anhydride or halomaleate ester may be converted to terminal carboxyl groups by conventional hydrolysis. The resulting dicarboxylic terminated polymer can be copolymerized with glycols to form polyesters or with diamines to form polyamides having a graft copolymer structure. Alternatively, the maleic anhydride or ester terminal group or the polymer can be used in the condensation polymerization with the glycols or diamines. The vicinal hydroxy or carboxyl terminated polymers of the invention can also be copolymerized with epoxy compounds, and the imine compounds, such as ethyleneimine,

The placement of the sidechain in the polymer backbone is dependent on the terminal group of the macromolecular monomer and the reactivity of the comonomer.

The macromolecular monomers of the invention are stable in storage and do not significantly homopolymerize. Furthermore, the macromolecular monomer copolymerizes through the terminal double bond or reactive end group and is not incorporated into the polymeric backbone by grafting reactions to the polymer of the macromolecular monomer segment.

As indicated hereinabove, the macromolecular monomers of the invention copolymerize with commercial vinyl monomers in a predictable manner as determined by relative reactivity ratios. It can be shown that the instantaneous copolymer equation:

simply reduces to the approximation:

--- IU M 2 2 3. r (dMz/M2/dM /M (percent Conversion M /percent Conversion M The reactivity ratio, r can be estimated from a relatively low conversion sample of a single copolymrization experiment. The validity of this concept of a predictable and controllable reactivity of the macromolecular monomer can thereby be established. It has been shown that the reactivity of commercial monomers with the macromolecular monomers of the present invention with various end groups correlate with available literature values for reactivity ratios of r The method of the present invention permits the utilization of all types of polymerizable monomers for incorporation into backbone polymers, and makes it possible for the first time to design and build graft copolymers of controlled molecular structure, and of backbone and graft segments with different properties, such as hydrophobic and hydrophilic segments, crytalline and amorphous segments, polar and non-polar segments, segments with widely different glass transition temperatures, whereas prior work on SDS terblock copolymers had been limited to the incompatibility of glassy polystyrene blocks with rubbery polydiene blocks.

The copolymerization of the polymerizable macromolecular monomers with the comonomers may be conducted in a wide range of proportions. Generally speaking, a sufficient amount of the macromolecular monomer should be present to provide the chemically joining of at least one of the uniform molecular weight sidechain polymers to each backbone polymer, so that a noticeable effect on the properties of the graft copolymeric properties can be obtained. Since the molecular weight of the polymerizable macromolecular monomer generally exceeds that ,of the polymerizable comonomers, a relatively small amount of the polymerizable macromolecular monomer can be employed. However, the chemically joined, phase separated thermoplastic graft copolymers may be prepared by copolymerizing a mixture containing up to about 95 percent by weight, or more, of the polymerizable macromolecular monomers of this invention, although mixtures containing up to about 60 percent by weight of the polymerizable macromolecular monomer are preferred. Stated, otherwise, the resinous thermoplastic chemically joined, phase separated graft copolymer of the invention is comprised of 1) from 1 to about 95 percent by weight of the polymerizable macromolecular monomer having a narrow molecular weight distribution (i.e., a Mw/Mn of less than about 1.1), and (2) from 99 to about 5 percent by weight of a copolymerizable comonomer defined hereinabove.

The polymerizable macromolecular monomers copolymerize with the hereinabove referred to comonomers in bulk, in solution, in aqueous suspension and in aqueous emulsion systems suitable for the particular polymerizable macromolecular monomer, its end group and the copolymer employed. If a catalyst is employed, the polymerization environment suitable for the catalyst should be employed. For example, oilor solventsoluble peroxides such as benzoyl peroxides, are generally effective when the polymerizable macromolecular monomer is copolymerized with an ethylenically unsaturated comonomer in bulk, in solution in an organic solvent such as benzene, cyclohexane, hexane, toluene, xylene, etc., or in aqueous suspension. Water-soluble peroxides such as sodium, potassium, lithium and ammonium persulfates, etc. are useful in aqueous suspension and emulsion systems. In the copolymerization of many of the polymerizable macromolecular monomers, such as those with an ethylenically-unsaturated end group and a polystyrene, polyisoprene or polybutadiene repeating unit, an emulsifier or dispersing agent may be employed in aqueous suspension systems. In these systems, particular advantage can be achieved by dissolving the water-insoluble polymerizable macromolecular monomer in a small amount of a suitable solvent, such as a hydrocarbon. By this novel technique, the comonomer copolymerizes with the polymerizable macromolecular monomer in the solvent, in an aqueous system surrounding the solvent-polymer system. Of course, the polymerization catalyst is chosen such that it-will be soluble in the organic phase of the polymerization system.

As previously stated, various different catalyst systems can be employed in the present invention for the copolymerization process. It will be apparent to those skilled in the art that the particular catalyst system used in the copolymerization will vary, depending on the monomer feed and the particular end group on the macromolecular monomer. For example, when using a macromolecular monomer having a vinyl acetate end group, best results are generally obtained by employing free-radical catalyst systems. On the other hand, copolymerization utilizing isobutylene monomer feed with either an ally], methallyl or epoxy terminated macromolecular monomer, best results are accomplished by utilizing the cationic polymerization techniques. Since the particular polymerizable end group on the macromolecular monomer will depend on the comonomer feed employed because of the relative reactivity ratios, the polymerization mechanism commonly employed for the particular comonomer will be used. For example, ethylene polymerizes under free-radical, cationic and coordination polymerization conditions; propylene and higher alpha-olefins only polymerize under coordi- I nation polymerization conditions; isobutylene only polymerizes under cationic polymerizationconditions; the dienes polymerize by free-radical anionic and coordination polymerization conditions; styrene polymerizes under free-radical, cationic, anionic and coordination conditions; vinyl chloride polymerizes under freeradical and coordination polymerization conditions; vinylidene chloride polymerizes under free-radical po lymerization conditions; vinyl fluoride polymerizes under free-radical conditions; tetrafluoroethylene polymerizes under free-radical and coordination polymerization conditions; vinyl ethers polymerize under cationic and coordination polymerization conditions; vinyl esters polymerize under free-radical polymerization conditions; acrylic and methacrylic esters polymerize under free-radical, anionic and coordination polymerization conditions; and acrylonitrile polymerizes under free-radical, anionic and coordination polymerization conditions.

It will be understood by those skilled in, the art that the solvent, reaction conditions and feed rate will be partially dependent upon the type of catalyst system utilized in the copolymerization process. One of the considerations, of course, will be that the macromolecular monomer be dissolved in the solvent system utilized. lt is not necessary, however, for the monomer feed to be soluble in the solvent system. Generally, under these conditions during the formation of the copolymer, the graft copolymer will precipitate out of the solvent wherein it can be recovered by techniques known in the polymer art.

The temperature and pressure conditions during the copolymerization process will vary according to the type of catalyst system utilized. Thus, in the production of low density polyolefin backbones under free-radical conditions, extremely high pressures will be employed. On the other hand, the high density substantially linear polyolefin backbone polymers produced by the coordination type catalyst generally will be prepared under moderately low pressures.

When preparing graft copolymers having a polyolefin backbone of ethylene or propylene or copolymers of ethylene and propylene together with a macromolecular monomer, it is preferred to employ a coordination catalyst known in the art as the Ziegler catalyst and Natta catalysts (the latter being commonly used for polypropylene). That is, materials advanced by Professor-Dr. Karl Ziegler of the Max Planck Institute of Mulheim, Rugh, Germany, and Dr. Giulio Natta of Milan, Italy. Some of these catalysts are disclosed in Belgian Pat. No. 533,362, issued May 16, 1955, and U.S. Pat. Nos. 3,113,115 and 3,257,332 to Ziegler et al. These catalysts are prepared by the interaction of a compound of transition metals of group IV-Vlll in the periodic table, the catalyst, and an organometallic compound derived from group l-IIl metals, as co-catalyst. The latter are compounds such as metal hydrides and alkyls capable of giving rise to hydride ions or carbanions, such as trialkyl aluminum. Compounds of the transition elements have a structure with incomplete d-shells and in the lower valence states, can associate with the metal alkyls to form complexes with highly polarized bonds. Those elements hereinabove referred to as the catalysts are preferably titanium, chromium, va-

. nadium, and zirconium. They yield the best Ziegler catalysts by reaction of their compounds with metal alkyls.

As previously stated, the solvent system utilized will most conveniently be the solvent employed in the preparation of the macromolecular monomer. Solvents useful for the polystyrene macromolecular monomers are those which dissolve polystyrene. Typical solvents for polystyrene include cyclohexane, benzene, toluene, xylene, decalin, tetralin, etc.

The copolymerization reaction may be conducted at any suitable temperature, depending on the particular catalyst, macromolecular monomer, monomer feed, resulting graft copolymer and solvent used. Generally, the graft copolymerization will be conducted at a temperature of from about C to about 500C, preferably from about C to about 100C.

The graft copolymerization reaction is preferably conducted by placing a predetermined amount of the macromolecular monomer dissolved in the appropriate solvent in the reactor. The polymerization catalyst and monomer are thereafter fed into the solvent system to produce the graft copolymer.

It is generally desirable to provide a graft copolymer having at least about 2 percent macromolecular monomer incorporated in the backbone polymeric material, however, satisfactory results can be obtained with up to about 40 percent by weight macromolecular monomer incorporation. Preferably, the graft copolymers of the macromolecular monomer used in the copolymerization process. For example, if a graft copolymer having 10 percent by weight incorporation of the macromolecular monomer into the backbone polymer is desired, one simply employs 10 parts by weight of the macromolecular monomer for each parts by weight of the monomer feed.

Following the procedures outlined above, graft copolymers having unique combinations of properties are produced. These unique combinations of properties are made possible by the novel process herein which forces the compatibility of otherwise incompatible polymeric segments. These incompatible segments segregate into phases of their own kind.

The chemically joined, phase separated graft copolymers of the invention microscopically possess a controlled dispersion of the macromolecular sidechain in one phase (domain) within the backbone polymer phase (matrix). Because all of the macromolecular monomer sidechain domains are an integral part or interposed between large segments of the backbone polymer, the resulting graft copolymer will have the properties of a cross-linked polymer, if there is a large difference in the Tg or Tm of the backbbone and sidechain segments. This is true only up to the temperature required to break the thermodynamic cross-link of the dispersed phase. In essence, a physically cross-linked (as opposed to chemical cross-linked) type polymer can be made that is reprocessable and whose properties are established by simple cooling, rather than vulcanization or chemical cross-linking.

The graft copolymers of the present invention are differentiated from the macroscopic opaque and weak blends of incompatible polymers of the prior art. The graft copolymers of this invention contain separate phases which are chemically joined and the dispersion of one segment into the matrix polymer is on a microscopic level and below the wavelength of light of the matrix polymer. The graft copolymers herein are, therefore, transparent, tough, and truly thermoplastic.

An illustrative example of the present invention includes combining the advantageous properties of polystyrene with the advantageous properties of polyethylene, although these two polymers normally are incompatible iwth one another and a mere physical mixture of these polymers has very little strength and is not useful. To combine these advantageous properties in one product, it is necessary that the different polymeric segments be present as relatively large segments. The properties of polystyrene do not become apparent until the polymer consists essentially of at least about 20 re curring monomeric units. This same relationship applies to the polymeric segments present in the graft copolymers herein, i.e., if a graft copolymer comprising polystyrene segments is to be characterized by the advantageous properties of polystyrene, then those polystyrene segments must, individually, consist essentially of at least about recurring monomeric units. This relationship between the physical properties of a polymeric segment in its minimum size is applicable to the polymeric segment of all graft copolymers herein. In general, the minimum size of a polymeric segment which is associated with the appearance of the physical properties of that polymer in the graft copolymers herein is that which consists ofabout 20 recurring monomeric units. Preferably, as noted earlier herein, the polymeric segments both of the copolymeric backbone and the sidechains, will consist essentially of more than about 30 recurring monomeric units. However, as it is well-known, the highly beneficial properties of polymers such as polystyrene are generally apparent when the polymer has a molecular weight of from about 5,000 to about 50,000, preferably from about 10,000 to about 35,000, more preferably 12,000 to about 25,000.

The polymeric segments of the graft copolymers of the invention may themselves be homopolymeric or they may be copolymeric. Thus, a graft copolymer of this invention may be prepared by the copolymerization of ethylene, propylene, and a terminated polystyrene containing a polymerizable alpha-olefin end group. The uninterrupted polymeric segments of the backbone of such a graft copolymer will be copolymeric segments of ethylene and propylene.

The graft copolymers comprising polymeric segments having fewer than about 20 recurring monomeric units are, nevertheless, useful for many applications, but the preferred graft copolymers are those in which the various polymeric segments have at least about 20 recurring monomeric units.

Although, as indicated, the graft copolymers herein are characterized by a wide variety of physical properties, depending on the particular monomers used in their preparation, and also on the molecular weights of the various polymer segments within a particular graft copolymer, all of these graft copolymers are useful, as tough, flexible, self-supporting films. These films may be used as food-wrapping material, paintersdropcloths, protective wrapping for merchandise displayed for sale, and the like.

Graft copolymers of the macromolecular monomer, polystyrene, with ethylene-propylene, isobutylene, or propylene oxide monomers have been found to be stable materials that behavelike vulcanized rubbers, but

are thermoplastic and reprocessable.- Thus, an extremely tough, rubbery plastic is obtained without the inherent disadvantages of a vulcanized rubber. These copolymerized rubber-forming monomers with the macromolecular monomers of the present invention have the additional use as an alloying agent for dispersing additional rubber for impact plastics.

Just as metal properties are improved by alloying, so are polymer properties. By adding the appropriate amount of an incompatible material to a plastic in a microdispersed phase, over-all polymer properties are improved. A small amount ofincompatible polybutadiene rubber correctly dispersed in polystyrene gives high impact polystyrene. The key to this microdispersion is a small amount of chemical graft copolymer that acts as a flux for incorporating the incompatible rubber.

In a similar manner, a copolymer of the macromolecular monomer of the present invention can be the flux for incorporating or dispersing incompatible polym e rs into new matrices making possible a whole new line of alloys, impact plastics, malleable plastics and, easy-toprocess plastics.

The use of the graft copolymers as alloying agents is particularly exemplified in the case of polyethylenepolystyrene blends. As it is well-known, polyethylene and polystyrene are incompatible when blended together. However, when using the graft copolymers of the present invention as an alloying agent, the polyethylene and polystyrene phases can be conveniently joined.

For example, a blend prepared by mixing to 51 parts by weight ofcommercial polyethylene (either low or high density); 10 to 49 parts by weight of commercial polystyrene and 5 to 30 parts by weight of a graft copolymer of the present invention comprising polystyrene sidechains and a polyethylene backbone are useful in making automobile parts, such as inner door panels, kick panels, and bucket seat backs, or appliance parts such as television components. Such blends are also useful as structural foams, sheets and films, containers and lids in packaging, beverage cases, pails, in the manufacture of toys, molded sheets in furniture, hot mold adhesives and computer and magnetic tapes.

The use of the graft copolymers of the present invention as an alloying agent offers a distinct advantage over the prior art blends, inasmuch as the plastic blend can be processed with minimized phase separation of the polystyrene and polyethylene polymers in the blend. The strength of the novel blends of the present invention is also improved over the blends of the prior art.

lf'polystyrene in the macromolecular monomer is replaced by a poly(alpha-methylstyrene) and is copolymerized with ethylene, a similar polyblend can be prepared as described above. However, these blends will have heat stability which will allow the resulting plastics to be'useful in making hot water pipes, sheets in warm areas, and automobile parts, having oxidative stability over rubber-containing materials. These plastics also have utility in preparing reinforced fiberglass and fillers due to their good adhesion to fiberglass. Polyblends of poly(alpha-methylstyrene) graft copolymer with large amounts, i.e., 51-90 percent by weight of poly(alpha-methylstyrene) and 10-49 percent polyethylene, exhibit a higher heat distortion, together with high impact strength and high modulus. These plastics are useful in various engineering applications and in the manufacture of parts for aircraft, auto bodies, recreational vehicles, appliances, gears, bearings, etc.

Another useful blend utilizing the graft copolymers of the present invention comprises mixing 10 to 49 parts of low density polyethylene, 51 to 91 parts by weight of poly(alpha-methylstyrene) and zero to 30 parts by weight of polystyrene and 5 to 30 parts by weight of the graft copolymer of the present-invention comprising polyethylene backbone with poly(alphamethylstyrene) or polystrene sidechains. The blend is extruded in a mill and the resultant plastic is found useful in making appliances such as coffee makers, humidifers, high intensity lamps, color television sets, kitchen-range hardware, blenders, mixers, and electric toothbrushes. These plastics are also useful in preparing recreational vehicles such as snowmobile parts and helmets; machine parts such as gears, bearings; plumbing parts such as shower heads, valves, fittings and ballcocks; and motor housing, stamping, lawn sprinklers, stereo tape or cartridges, etc.

The reinforcement of plastics by adding glass fibers or other materials is difficult to achieve because of poor wettingcharacter of many basic polymers. The macromolecular monomers of the present invention,

particularly those containing reactive polystyrene, have a tendency to wet and bond to glass with facility. By proper dispersion of glass in a macro molecular copolymer, it is possible to upgrade the bond between the dispersed phase and glass. Thus, the macromolecular graft copolymers of the present invention can also be used as reinforcing adhesion aids to glass fibers.

The invention is illustrated further by the following examples which, however, are not to be taken as limit- CH CH CH )CH 3 2 3 ing in any respect. In each case, all materials should be pure and care should be taken to keep the reacted mixtures dry and free of contaminants. All parts and percentages, unless expressly stated to be otherwise, are by weight.

Preparation Of Macromolecular Monomer Sidechains Having Uniform Molecular Weight Example 1 a. Preparation Of Polystyrene Terminated With Allyl Chloride A stainless steel reactor is charged with 76.56 parts of A.C.S. grade benzene (thiophene-free), which had been pre-dried by Linde molecular sieves and calcium hydride. The reactor is heated to 40C and 0.015 parts of diphenylethylene is added to the reactor by means of a hypodermic syringe. A 12.1 percent solution of secbutyl lithium in hexane is added to the reactor portionwise until the retention of a permanent orangeyellow color, at which point an additional 0.885 parts (1.67 moles) of sec-butyl lithium solution is added, followed by the addition of 22.7 parts (218 moles) of styrene over a period of 44 minutes. The reactor temperature is maintained at 3642C. The living polystyrene is terminated by the addition of 0.127 parts of allyl chloride to the reaction mixture. The resulting polymer is precipitated by the addition of the alphaolefin terminated polystyrene-benzene solution into methanol, whereupon the polymer precipitates out of solution. The alpha-olefin terminated polystyrene is dried in an air circulating atmosphere drier at 40-45C and then in a fluidized bed to remove the trace amounts of methanol. The methanol content after purification is parts per million. The molecular weight of the polymer, as determined by membrane phase osmometry, is 15,400 (theory: 13,400) and the molecular weight distribution is very narrow, i.e., the Mw/Mn is less thanv 1.05. The macromolecular monomer has the following structural formula:

CH CH 2 2 b. The procedure of Example 1(a) is repeated using, in place of allyl chloride, an equivalent amount of methallyl chloride to produce a methallyl terminated polystyrene.

c. The procedure of paragraph (a) is repeated using, in place of styrene, an equivalent amount of ethylene oxide to produce a crystalline polyoxyethylene living polymer. The living polymer is terminated by the addition of a molar equivalent amount of vinylbenzyl chloride to produce a polymer having the following struc tural formula:

EXAMPLE 2 a. Preparation Of Poly(alpha-methylstyrene) Terminated With Allyl Chloride A solution of 472 grams (4.0 moles) of alphamethylstyrene in 2500 ml. of tetrahydrofuran is treated dropwise with a 12 percent solution of n-butyl lithium in hexane until the persistence of a light red color. An additional 30 ml. (0.0383 mole) of this n-butyl lithium solution is added, resulting in the development of a bright red color. The temperature of the mixture is then lowered to -C, and after 30 minutes at this temperature, 4.5 grams (0.06 mole) of allyl chloride is added. The red color disappears almost immediately indicating termination of the living polymer. The resulting colorless solution is poured into methanol to precipitate the alpha-olefin terminated poly(alpha-methylstyrene) which is shown by vapor phase osmometry to have a number average molecular weight of 11,000 (theory: 12,300) and the mole cular weight distribution is very narrow, i.e., the Mw/Mn is less than 1.05. The macromolecular monomer produced has the following structural formula:

Cl-l

CH CH CH -C 2 2 2 CHCH-CH 1] CH Ct 2 2 CH -CH CH CH I CH c. methacrylonitrile, terminating with a molar equivalent of vinylbenzyl chloride to produce a polymer having the following structural formula:

, CN n d. methyl methacrylate, terminating with vinylbenzyl methylstyrene in 2500 ml. of tetrahydrofuran is treated chloride to produce a polymer having the following dropwise with a 12 percent solution of t-butyl lithium in pentane until the persistance of a light red color.

3 l -c -o cu cu cu CH C I 0011 n e. N,N-dimethylacrylamide, terminating with p- Thereupon, an additional 15.0 ml. (0.03 mole) of the vinylbenzyl chloride to produce a polymer having the t-butyl solution is added, resulting in the development following structural formula: 7 of a bright red color. The temperature of the mixture H H H (CH c 0 CH2 sin c c c 2 N(CH n EXAMPLE 3 is then lowered to 80C, and after 30 minutes at that temperature, 5.6 ml. of diphenyl ethylene is added. The resulting mixture is poured into 5.0 ml. (0.04 mole) of vinyl chloroacetate and the thus-terminated A Solution of one p of p y ethylene in 2500 poly(alpha-methylstyrene) is precipitated with metha- Preparation of Polystyrene Terminated with Vinyl Chloroacetate of Cyclohexane at is treated portionwise with nol and separated by filtration. lts'number average moa 12 percent solution of secbutyl lithium in cyclohexlecular weight as determined by vapor phase osmomeam until the persistence of a light red color, at which try, i 14 230 h 12,065) d the molecular Po a additional 18 mole) 0f h sec-butyl weight distribution is very narrow. The macromolecl thium iS added, fo o ed y 312 g m moles) of ular monomer produced has the following structural styrene. The temperature of the polymerization mixf l l l ll c11 cu (CH3) cu ea c 011 cu cocu CH ture is maintained at 40C for 30 minutes, whereupon where-in n has a value such that the molecular weight the living polystyrene is capped by treatment with 8 ml. of the polymer is 14,280.

(0.040 mole) of diphenyl ethylene, then terminated by treatment with 6 ml. (0.05 mole) of vinyl chloroace- EXAMPLE 5 tate. The resultin olymer is recipitated by addition of the cyclohexan e solution to methanol and the poly- Preparanor? of Polystyrene Termmated wlth mer is separated by filtration. Its number average movmyl'z'chlomethyl Ether lecular weight, as determined by vapor phase osmome- A solution of one drop of diphenyl ethylene at 40C try, is 12,000 (theory: 13,265), and the molecular is treated portionwise with a 12 percent solution of tweight distribution is very narrow, i.e., the lT/l w/mn is butyl lithium in pentane until the persistance of a light less than 1.06. The macromolecular monomer prored color, at which point an additional 30 ml. (0.04 duced has the following structural formula: mole) of the t-butyl lithium solution is added, followed 0 ll CH CH (CH )C CH CH CH -CH C0CH I CH wherein n has a value such that the molecular weight by 312 grams (3.0 moles) of styrene. The temperature of the polymer is 12,000. V of the polymerization mixture ismaintained at 40C for 30 minutes, whereuopn the living polystyrene is termi- EXAMPLE 4 nated by treatment with 8 ml. (0.08 mole) of vinyl-2- chloroethyl ether. The resulting polymer is precipitated by addition of the benzene solution to methanol and the polymer is separated by filtration. lts number aver- A solution of 357 grams (3.0 moles) of alphaage molecular weight, as determined by vapor phase Preparation of Poly(alpha-methylstyrene) Terminated with Vinyl Chloroacetate osmometry, is 7,200 y 7,870) and theiloltgular wherein n has a value such that the molecular weight weight distribution is very narrow, i.e., the Mw/Mn is of the polymer is 10,000, less than 1.06. The macromolecular monomer prob. Acrylyl chloride is substituted for methacrylyl dllCed has the f l g Structural fOI'mUlaI chloride in the above procedure to give an acrylic acid ester end group on the polystyrene chain.

c. Allyl chloride is substituted for methacrylyl chloride in procedure (a) to produce an ally] ether termi- (CH c H H CH OCH CH nated polystyrene. I

3 3 2 2 2 2 d. Methallyl chlorlde ls substituted for methacrylyl n it) chloride in procedure (a) to produce methallyl ether terminated polystyrene.

e. Maleic anhydride is substituted for methacrylyl chloride in procedure (a), followed by protonation wherein n has a value such that the molecular welght with water to produce polystyrene terminated with the of the polymer is half ester of maleic acid.

EXAMPLE 6 f. lipichlorohydrin is substituted for methacrylyl chlorlde to produce an epoxy ether termlnated polysty- Preparatlon of Polystyrene Termlnated wlth rene Eplchlorohydrm g. The procedure of (a) is repeated using in place of A benzene solution of living polystyrene is prepared Styrene, equiiaient amount of isoprene and in Place in Example 5 and terminated by treatment with 10 of n-butyl lithium an equivalent amount of sec-butyl grams (0.10 mole) of epichlorohydrin. The resulting lithium to produce primarily a rubbery cis-1,4- terminated polystyrene is precipitated with methanol POlYiSOPIeHe. The low Tg l ing polymer iS terminated and separated by filtration. Its molecular weight, as by the addition of a molar equivalent, based on secshown by vapor phase osmometry, is 8,660 (theory: butyl lithium, ethylene oxide as a capping agent, fol- 7,757) and its number average molecular weight distrilowed by a molar equivalent amount of allyl chloride to bution is very narrow. The macromolecular monomer produce a polymer predominantly having the following produced has the following structural formula: structural formula:

CH CH (CH )CH Clk {PR CH CH OCH CH I CH C I C n CH H Methacrylyl Chloride EXAMPLE 8 (CH .-C ca H ca cu \u 6 n Preparation of Polystyrene Terminated with wherein n has a value such that the molecular weight 40 of the P y A stainless steel reactor is charged with 32 gallons of EXAMPLE 7 A.C.S. grade benzene (thiophene-free), which had been predried by Linde molecular sieves and calcium Preparatlon of Polystyrene Terminated Wlth hydride. The reactor is heated to a temperature of be- Methacrylyl chloride tween 38-40C and 10 ml. of diphenyl ethylene is To a solution of 0.2 m1. of diphenyl ethylene in 2,500 added to the reactor y means of a hypodermic Syringe ml. of benzene there is added dropwise a 12 percent Ah 1 Percent Solution of secon ry butyl lithium in lution of n-butyl lithium in hexane until the persistence heXahe is added to the reae or portionwise until the reof a light reddish-brown color. An additional 24 ml. 50 tention ofa permanent orange-yellow color is obtained (0.031 mole) of this n-butyl lithium solution is added, at WhiCh Point an additional Pounds Of and then, 416 grams (4.0 moles) of styrene, resulting the secondary butyl lithium in hexane is added to the in the development of an orange color. A temperature reactor, followed by the addition of 82.5 pounds of pu-- of 40C is maintained throughout by external cooling rifled styrene over a period of 1 hour and 40 minutes. and by controlling the rate at which the styrene is The reactor temperature is maintained at 38-40C.

added. This temperature is maintained for an addi- Theliving polystyrene is capped by the addition of0.28 tional 30 minutes after all of the styrene has been pounds of ethylene oxide and the reaction solution added, and then is lowered to 20C, whereupon 4.4 changes from a red-orange color to yellow. The resultgrams (0.1 mole) of ethylene oxide is added, causing ing capped living polystyrene is thereafter reacted with the solution to become colorless. The living polymeris 260 ml. of methacrylyl chloride and the solution terminated by reaction with 10 ml. (0.1 mole) of mechanges to a very pale yellow color. The methacrylate thacrylyl chloride. The resulting polymer has a number terminated polystyrene is precipitated by the addition average molecular weight as shown by vapor phase osof the polymer benzene solution into methanol, wheremometry of 10,000. The macromolecular monomer upon the polymer precipitates out of solution. The has the following structural formula: polymer is dried in an air circulating atmosphere drier mometry, is 13,400 and the molecular weight distribu- 0 at 40-45C and then ina fluidized bed to remove the ll trace amounts of methanol. The molecular weight of g g g g H E the polymer as determined by membrane phase os- I 3 tion is very narrow, i.e., the Mw/Mn is less than 1.05.

EXAMPLE 9 Preparation of Polystyrene Terminated with Maleic Anhydride A stainless steel reactor is charged with 2.5 liters of A.C.S. grade benzene (thiophene-free), which had been predried by Linde molecular sieves and calcium hydride. The reactor is heated to 40C and 0.2 ml. of diphenyl ethylene is added to the reactor by means of a hypodermic syringe. A 12.1 percent solution of secbutyl lithium in hexane is added to the reactor portionwise until the retention of a permanent orange-yellow color is obtained (0.7 ml.), at which point an additional 22.3 ml. of'sec-butyl lithium solution is added, followed by the addition of 42 1 .7 grams of styrene over a period of 16 minutes. The reactor temperature is maintained at 4045C. Five minutes after styrene addition is completed, ethylene oxide is added from a lecture bottle subsurface intermittently until the solution is water white. One hour after ethylene oxide addition is complete, 20.55 ml. of maleic anhydridebenzene solution (the maleic anhydride solution was prepared by dissolving 84 grams of maleic anhydride in 550 grams of purified benzene) is added to the capped living polymer. One hour after the addition of the maleic anhy-.

dride solution, the contents of the reactor are discharged and precipitated in methanol. The maleic half ester terminated polystyrene had a molecular weight of about 14,000, as determined by Gel Permeation Chromatography. The polymerizable macromolecular monomer has a structural formula represented as follows:

Chloride C.P. grade 1,3-butadiene (99.0 percent purity) is condensed and collected in' l-pint soda bottles. These bottles had been oven baked for 4 hours at 150C, nitrogen purged during cooling, and capped with a perforated metal crown cap using butyl rubber and polyethylene film liners. These bottles containing the butadiene are stored at lC with a nitrogen pressure head (10 psi) in a laboratory freezer before use. l-lexane solvent is charged to the reactors and heated to 50C, followed by the addition of 0.2 ml. of diphenyl ethylene by way of a syringe. Secondary butyl lithium is added dropwise via syringe to the reactor until the red diphenyl ethylene anion color persists for at least about 10-15 minutes. The reactor temperature is lowered to 0C, and 328.0 grams of butadiene is charged into the polymerization reactor, followed by the addition of 17.4 ml. (0.02187 mole) of a 12 percent secondary butyl lithium solution in hexane, when half of the butadiene charge has been added to the reactor. The butadiene is polymerized for 18 hours in hexane at 50C. Following the polymerization, 400 ml. portions of the anionic polybutadiene solution in the reactor is transferred under nitrogen pressure into capped bottles. Allyl chloride (0.48 ml., 0.00588 mole) is injected into each of the bottles. The bottles are clamped in water baths at temperatures of 50C and C for periods of time ranging up to 24 hours. The samples in each of the bottles are short stopped with methanol and lonol solution and analyzed by Gel Permeation Chromatography. Each of the samples is water white and the analysis of the Gel Permeation Chromatography scans reveals that each of the samples had a narrow molecular weight distribution.

Several comparison samples were conducted in bottles coming from the same lot of living polybutadiene, which were capped with 2-chlorobutane (0.4 ml., 0.00376 mole) as the terminating agent. The resulting polymers terminated with 2-chlorobutane were yellow in color and after standing for a period of 24 hours at 70C, appeared to have a broad molecular weight distribution as revealed by the Gel Permeation Chromatography scan. It is clear that the reaction and reaction product of 2-chlorobutane with anionic polybutadiene are different than the reaction and reaction product of allyl chloride and anionic polybutadiene.

EXAMPLE 11 Preparation of Methacrylate Terminated Polyisoprene A l-gallon Chemco Glass-bowl reactor is charged with 2.5 liters of purified heptane which had been predried by a Linde molecular sieve and calcium hydride, followed by the addition of 0.2 ml. of diphenyl ethylene as an indicator and the reactor is sterilized with the dropwise addition of tertiary butyl lithium solution (12 percent in hexane) until the retention of the characteristic light yellow color is. obtained. The reactor is heated to 40C and 19.9 ml. (0.025 mole) of a 12 percent solution of tertiary butyl lithium in hexane is injected into the reactor via hypodermic syringe, followed by the addition of 331.4 grams (4.86 moles) of isoprene. The mixture is allowed to stand for 1 hour at 40C and 0.13 mole of ethylene oxide is charged into the reactor to cap the living polyisoprene. The capped living polyisoprene is held at 40C for 40 minutes, whereupon 0.041 mole of methacrylyl chloride is charged 'into the reactor to terminate the capped living polymer. The mixture is held for 13 minutes at 40C, followed by removal of the heptane solvent by vacuum stripping. Based upon the Gel Permeation Chromatography scans for polystyrene, the molecular weight of the methacrylate terminatedpolyisoprene by Gel Permeation Chromatography was about 10,000 (theory: 13,000). The methacrylate terminated polyisoprene macromolecular monomer had a structural formula represented as follows:

CH I CH3 H EXAMPLE 12 Preparation of Alpha-Olefin Terminated Polyisoprene A one-gallon Chemco glass-bowl reactor is charged with 2.5 liters of purified heptane which had been predried by a Linde molecular sieve and calcium hydride, followed by the addition of 0.2 ml. of diphenyl ethylene as an indicator. The reactor and solvent are sterilized by the dropwise addition of tertiary butyl lithium solution (12 percent in hexane) until the retention of the characteristic light yellow color is obtained. The reactor is heated to 40C and 19.03 ml. (0.02426 mole) of tertiary butyl lithium solution is injected into the reactor via hypodermic syringe, followed by the addition of 315.5 grams (4.63 moles) of isoprene. The polymerization is permitted to proceed at 50C for 66 minutes and at this time 2.0 ml. (0.02451 mole) of allyl chloride is added to the living polyisoprene. The terminated polyisoprene is held at 50C for 38 minutes, whereupon the polymer is removed from the reactor to be used in copolymerization reactions. The polymer was analyzed by Gel Permeation Chromatography and had a very narrow molecular weight distribution, i.e., an Mw/Mn of less than about 1.06. The theoretical molecular weight of the polymer is 13,000. The polymerizable macromolecular monomer had a structural formula represented as follows:

EXAMPLE 13 Polymerization of Styrene with Vinyl Lithium To a one gallon Chemco reactor, there is added 2,500 ml. of tetrahydrofuran and cooled to 15C., at which time 6.5 ml. of a 11.2 percent solution of vinyl lithium in tetrahydrofuran (0.2 mole lithium) is added to the reactor, imparting a light tan color to the solution. The vinyl lithium was purchased from Alpha Inorganics Ventron of Beverly, Mass, as a two molar solution in tetrahydrofuran. Analysis of the solution by several methods showed that the solution contained 11.2 percent active lithium. After the vinyl lithium solution is added, a 0.25 mole styrene charge is added to the reactor via syringe with the observation of a small exotherm of about 1C (the reactor temperature is controlled by liquid nitrogen cooling coils inside the reactor at a temperature of 15C). Ten minutes after the styrene is added, 3.6 ml. of water is added to the reactor, resulting in an almost immediate change in color from deep orange-brown to water white and a considerable gas evolution is observed (the internal pressure in the reactor increased from 8 psig to 12 psig). A sample is taken from the head space (about 2.5 liters in volume) and from the liquid phase at the same time (the two samples are analyzed and identified as containing large amounts of ethylene). The styrene polymer is withdrawn from the reactor and analyzed. The GPC molecular weight of the polystyrene is 108,000, as measured against the Pressure Chemical Company sample 2(b) standard certified as MW/Mn 1.06, MW 20,800 i 800 and Mn 20,200 i 600. Measured against the same standard, the weight average molecular weight of the polymer is 99,000 and the number average molecular weight is 66,000. The polydispersity of the polymer is 1.49. Based upon the limiting polydispersity of about 1.33 for living polymers, as indicated in Henderson et al., Macromolecular Reviews, Vol. 3, lnterscience Publishers, page 347 (1968), several side reactions obviously occur when using vinyl lithium as a polymerization initiator. In addition, the broad molecular weight distribution and the inability to control the molecular weight of the polymer is indicative that the initiation rate of vinyl lithium is extremely slow. Accordingly, the vinyl lithium initiated polystyrene is not suitable in the preparation of the graft copolymers of the present invention in preparing chemically joined, phase separated graft copolymers, which have sidechains of controlled and uniform molecular weights.

Attempted copolymerization of the vinyl lithium initiated polystyrene with methyl methacrylate and acrylonitrile under free-radical conditions only results in a mixture of polystyrene and the respective poly(methyl methacrylate) or polyacrylonitrile. Also, attempted copolymerization of the alpha-olefin terminated polystyrene of Example 1(a) with methyl methacrylate and acrylonitrile under free-radical conditions only resulted in a mixture of homopolymers as determined by IR analysis of the benzene and cyclohexane extracts. This result is expected due to the inability of alpha-olefins to polymerize under free-radical conditions.

Preparation Of Graft Copolymers Having Macromolecular Monomers Integrally Polymerized Into the Backbone EXAMPLE 14 Preparation of Graft Copolymer from Poly(alpha-methylstyrene) Macromolecular Monomer Terminated with Allyl Chloride and Ethylene A solution of 20 grams of poly(alpha-methylstyrene) macromolecular monomer terminated with allyl chloride and having an average molecular weight of 10,000 prepared as in Example 2(a) in mljof cyclohexane is prepared and treated with 5.5 ml. of 0.645 M (9.1 percent solution) diethyl aluminum chloride in hexane and 2 ml. of vanadium oxytrichloride, then pressured with ethylene to 30 psig. This system is agitated gently for about 1 hour at 30C, whereupon a polymeric material precipitates from the solution. It is recovered by filtration and pressed into a thin transparent film which is tough and flexible.

EXAMPLE 15 a. Preparation of Graft Copolymer Having a Polyethylene Backbone and Polystyrene Sidechains One gram of the alpha-olefin terminated polystyrene of uniform molecular weight prepared in Example 1(a) is dissolved in 1500 ml. of cyclohexane and charged into a 2-liter Chemco reactor. The reactor is purged with prepuritied nitrogen for 30 minutes, and 22 ml. of 25 percent ethylaluminum sesquichloride solution (in heptane) is added. The reaction is pressured to 40 psi with 20 grams of ethylene into the solution. Thereafter, 0.1 ml. of vanadium oxytrichloride is added and the ethylene pressure drops from 40 psi to 1 psi in about 1 

1. COPOLYMERIZING: A. FROM ABOUT 1 TO ABOUT 95 PERCENT BY WEIGHT OF A POLYMERIZABLE MACROMOLECULAR MONOMER COMPRISING A LINEAR POLYMER OR COPOLYMER HAVING A MOLECULAR WEIGHT IN THE RANGE OF FROM ABOUT 5,000 TO ABOUT 50.000 AND HAVING A SUBSTANITALLY UNIFORM MOLECULAR WEIGHT DISTRICBUTION, SUCH THAT ITS RATIO OF MW/MN IS LESS THAN ABOUT 1.1, SAID MACROMOLECULAR MONOMER BEING FURTHER CHARACTERIZED AS HAVING NO MORE THAN ONE POLYMERIZABLE MOLETY PER LINEAR POLYMER OR COPOLYMER CHAIN, SAID POLYMERIZABLE MOIETY BEING ON THE END OF THE CHAIN; AND B. FROM ABOUT 99 TO ABOUT 5 PERCENT BY WEIGHT OF AT LEAST ONE COPOLYMERIZABLE COMONOMER, SAID COPOLYMERIZABLE COMONOMERS FORMING THE POLYMERIC BACKBONES OF SAID GRAFT COPOLYMER AND SAID POLYMERIZABLE MACROMOLECULAR MONOMERS FORMING THE LINEAR POLYMERIC SIDECHAINS OF SAID GRAFT COPOLYMER, AND THE LINEAR POLYMERIC SIDECHAINS OF THE GRAFT COPOLYMER ARE COPOLYMERIZED INTO THE BACKBONE POLYMER THROUGH THE POLYMERIZABLE END GROUP ON SAID MACROMOLECUALR MONOMER, AND WHEREIN SAID COPLYMERIZABLE COMMONOMER UNITS OF THE BACKBONE ARE COMPRISED OF POLYMERIZED ETHYLENICALLYUNSATURATED MONOMERS, THE LINEAR POLYMERIC SIDECHAINS OF THE GRAFT COPOLYMER WHICH ARE COPOLYMERIZED INTO THE COPOLYMERIC BACKBONE ARE SEPARATED BY AT LEAST ABOUT 20 UNINTERRUPTED RECURRRING MONOMERIC UNITS OF SAID BACKBONE POLYMER; THE COPOLYMERIZATION AND DISTRIBUTING OF THE SIDE CHAINS ALONG THE BACKBONE POLYMERS BEING CONTROLLED BY THE RELATIVE REACTIVITY RATIOS OF THE POLYMERIZABLE END GROUP ON SAID MACROMOLECULAR MONOMER AND SAID COPOLYMERIZABLE COMMONOMER;
 2. SAID COPOLYMERIZATION BEING CONDUCTED IN AN AQUEOUS LATEX COPOLYMERIZATION MEDIUM, WHEREIN SAID POLYMERIZABLE MACROMOLECULAR MONOMER IS DISSOLVED IN A SMALL AMOUNT OF A SOLVENT THEREFOR, AND SAID SOLVENT AND POLYMERIZABLE MACROMOLECULAR MONOMER ARE EMULSIFIED IN WATER BY THE ACTION OF AN EMULSIFYING AGENT BEFORE THE COPOLYMERIZATION WITH SAID COPOLYMERIZABLE COMMONER, SAID COPOLYMERIZATION BEING INITIATED BY A POLYMERIZATION CATALYST WHICH IS SOLUBLE IN THE ORGANIC PHASE OF THE POLYMERIZATION SYSTEM; AND
 2. said copolymerization being conducted in an aqueous latex copolymerization medium, wherein said polymerizable macromolecular monomer is dissolved in a small amount of a solvent therefor, and said solvent and polymerizable macromolecular monomer are emulsified in water by the action of an emulsifying agent before the copolymerization with said copolymerizable comonomer, said copolymerization being initiated by a polymerization catalyst which is soluble in the organic phase of the polymerization system; and
 2. The process of claim 1, wherein at least one of said copolymerizable comonomers is a member selected from the group consisting of acrylic acid, methacrylic acid, the alkyl esters of acrylic and methacrylic acids, acrylonitrile, methacrylonitrile, acrylamide, mEthacrylamide, N,N-dimethylacrylamide, vinyl chloride, vinylidene chloride, vinylidene cyanide, vinyl acetate, vinyl propionate, vinyl chloroacetate, fumaric acid and esters, maleic anhydrides, acids and esters, and comonomeric mixtures thereof.
 2. said copolymerization being conducted in an aqueous suspension copolymerization medium comprising an aqueous phase, an organic phase suspended in said aqueous phase and at least one suspending agent, wherein said polymerizable macromolecular monomers are dissolved in said organic phase, said copolymerization being initiated by a polymerization catalyst which is soluble in the organic phase of said copolymerization medium.
 3. STOPPING THE COPOLYMERIZATION PRIOR TO THE FORMATION OF SUBSTANTIAL AMOUNTS OF HOMOPOLYMERS OF SAID BACKBONE POLYMER TO THEREBY OBTAIN A STABLE LATEX OF A SUBSTANTIALLY PURE, CHEMICALLY JOINED, PHASE SEPARATED THERMOPLASTIC GRAFT COPOLYMER.
 3. stopping the copolymerization prior to the formation of substantial amounts of homopolymers of said backbone polymer to thereby obtain a stable latex of a substantially pure, chemically joined, phase separated thermoplastic graft copolymer.
 3. The process of claim 1, wherein said macromolecular monomer is a methacrylate terminated polystyrene represented by the structural formula:
 4. The process of claim 1, wherein said solvent for said polymerizable macromolecular monomer is a hydrocarbon.
 5. The process of claim 1, wherein said emulsifying agent is calcium dodecylbenzene sulfonate.
 6. The process of claim 1, wherein said polymerization catalyst is lauroyl peroxide which has been dissolved in a small amount of a hydrocarbon.
 7. The stable latex produced by the process of claim
 1. 8. The stable latex produced by the process of claim
 3. 9. A process for preparing a suspension of a chemicall joined, phase separated thermoplastic graft copolymer comprising:
 10. The process of claim 9, wherein at least one of said copolymerizable comonomers is a member selected from the group consisting of acylic acid, methacrylic acid, the alkyl esters of acrylic and methacrylic acids, acrylonitrile, methacrylonitrile, acrylamide, methacrylamide, N,N-dimethylacrylamide, vinyl chloride, vinylidene chloride, vinylidene cyanide, vinyl acetate, vinyl propionate, vinyl chloroacetate, fumaric acid and esters maleic anhydries, acids and esters, and comonomeric mixtures thereof.
 11. The process of claim 9, wherein said organic phase contains a hydrocarbon which is a solvent for said polymerizable macromolecular monomers.
 12. The process of claim 9, wherein said suspending agent is comprised of a phosphate salt.
 13. The process of claim 9, wherein said suspending agent is comprised of a polyvinyl alcohol.
 14. The process of claim 9, wherein said polymerization catalyst is lauroyl peroxide which has been dissolved in said organic phase.
 15. The process of claim 9, wherein said polymerizable macromolecular monomers are comprised of methacrylate terminated polystyrene represented by the structural formula:
 16. The suspension produced by the process of claim
 9. 17. The suspension produced by the process of claim
 15. 